Iron-based superconducting permanent magnet and method of manufacture

ABSTRACT

The present invention provides for polycrystalline superconducting permanent magnets which are synthesized of doped superconducting (AE) Fe 2 As 2  compounds, where AE denotes an alkaline earth metal, such as Ba, Sr, Mg or Ca. The superconducting permanent magnets of the present invention can be magnetized in their superconducting state by induced currents, resulting in trapped magnetization that scales with the size of the bulk material. The magnitude of the trapped field has been demonstrated to be over 1 T and is predicted to be over 10 T if the technology is scaled, which is much higher than the capabilities of permanent magnets and other superconducting polycrystalline bulks currently known in the art.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation of and claims priority to International Patent Application No. PCT/US2016/025648, entitled “IRON-BASED SUPERCONDUCTING PERMANENT MAGNET AND METHOD OF MANUFACTURE”, filed Apr. 1, 2016 by the same inventors, which claims priority to U.S. Provisional Patent Application No. 62/141,659, entitled “IRON-PNICTIDE BULK SUPERCONDUCTING MAGNET AND METHOD OF MANUFACTURE”, having a filing date of Apr. 1, 2015, the entirety of which is hereby incorporated by reference.

STATEMENT OF GOVERNMENT INTEREST

This invention was made with government support under DMR1306785 and DMR1157490 awarded by the National Science Foundation under the Division of Material Research. The Government has certain rights in the invention.

FIELD OF THE INVENTION

This invention relates to superconducting materials and in particular to iron-based superconducting permanent magnet materials.

BACKGROUND OF THE INVENTION

Permanent magnets are only capable of generating magnetic fields of up to approximately 1 Tesla, thereby rendering them inadequate for applications that rely on higher magnetic fields, such as generators, motors, flywheels, magnetic levitation, magnetic resonance imaging (MRI) and research magnets. The generation of magnetic fields above 1 Tesla requires the use of electromagnets, which greatly increases the implementation cost of these technologies.

Since the discovery of iron-based superconductors in 2008, a tremendous amount of research has been focused on the synthesis and study of these superconductors. Much of the research has been driven by reports of properties that are very appealing for applications, including low anisotropy (around 1-2), high upper critical fields (H_(c2)) (in excess of 90 T) and intrinsic critical current densities (above 1 MAcm⁻² (0 T, 4.2 K)). Unfortunately, soon after their discovery the grain boundaries in these iron-based superconductor materials were observed to block current, similar to rare-earth barium cuprate (REBCO) materials such as YBa₂Cu₃O_(7-x) (YBCO), but to a somewhat lesser extent. Remarkably, fine-grain, randomly oriented K-doped BaFe₂As₂ (Ba122) has been synthesized with global critical current density around 10 kAcm⁻² (4.2 K, 10 T) and textured tapes of K-doped Ba122 and SrFe₂As₂ (Sr122) have now been produced that raise J_(c) by another order of magnitude.

While mechanically reinforced superconducting REBCO (Gd—Ba—Cu—O) materials are known in the art that produce record levels of trapped magnetic fields (up to 17.6 Tesla), these magnetically reinforced superconducting materials are limited in size (radius ≦50 mm) because grain boundaries in the material block current flow, forcing samples of the material to be grown as single crystals to eliminate the grain boundaries. In contrast the superconductor, MgB₂ is not subject to intrinsic current blocking and as such, can be manufactured as large diameter polycrystalline bulks to trap magnetic fields. However, the trapped magnetic field of MgB₂ has been shown to be limited to around 3 T, which is inadequate for high magnetic field applications.

Accordingly, what is needed in the art is a superconducting material having geometric versatility and improved magnetic field trapping of high magnetic fields at lower temperatures.

SUMMARY OF INVENTION

The present invention provides for polycrystalline materials which are synthesized of doped superconducting (AE) Fe₂As₂ compounds, where AE denotes an alkaline earth metal, such as Ba, Sr, Mg and Ca. The bulk materials of the present invention can be magnetized in their superconducting state by induced currents, resulting in bulk trapped magnetization that scales with the size of the bulk material. The magnitude of the trapped field has been demonstrated to be over 1 T and is predicted to be over 10 T if the technology is scaled, which is much higher than the capabilities of permanent magnets and other superconducting polycrystalline bulks currently known in the art. In the Fe-based polycrystalline superconducting permanent magnet of the present invention, the magnet is in a superconducting state, wherein the magnet is spontaneously exciting a magnetic field without the assistance of an external power supply to drive the excitation of the magnetic field within the permanent magnet.

In a particular embodiment, the present invention provides an Fe-based polycrystalline superconducting permanent magnet exhibiting a magnetic field greater than about 1 T at a temperature of less than about 40 K. The polycrystal comprises a square lattice of Fe forming a layered structure and the polycrystal may further comprise one or more of anion elements, including As, P, S, Se, Te, F or O.

In an additional embodiment, a method of manufacturing an Fe-based polycrystal superconducting permanent magnet is provided, including the steps of preparing an Fe-based powder, pressing the Fe-based powder into a first container, heat-treating the Fe-based powder in a second container and magnetizing the Fe-based polycrystal to provide an Fe-based polycrystalline superconducting permanent magnet at a temperature of less than about 40 K. Magnetizing the Fe-based polycrystal to provide an Fe-based polycrystalline superconducting permanent magnet may further include, magnetizing the Fe-based polycrystal using a magnetic field, a pulsed magnetic field, an electric field or an electromagnetic field.

Accordingly, the present invention provides a superconducting material having geometric versatility and improved magnetic field trapping of high magnetic fields at lower temperatures.

BRIEF DESCRIPTION OF THE DRAWINGS

For a fuller understanding of the invention, reference should be made to the following detailed description, taken in connection with the accompanying drawings, in which:

FIG. 1A illustrates an exemplary polycrystal of the superconducting permanent magnet, in accordance with an embodiment of the present invention.

FIG. 1B illustrates the crystalline structure of the Fe-based polycrystalline superconducting permanent magnet, in accordance with the present invention.

FIG. 2 illustrates the dimensions, relative to the magnetic field, of an exemplary Fe-based polycrystalline superconducting permanent magnet, in accordance with an embodiment of the present invention.

FIG. 3A illustrates a light microscopy image of a polished surface of a disk-shaped K-doped Ba122 bulk sample (10 mm diameter and 3.7 mm thick), in accordance with an embodiment of the present invention.

FIG. 3B illustrates Remnant (Happ=0) magneto optical images at 11 K the sample field-cooled under 120 mT, in accordance with an embodiment of the present invention.

FIG. 3C illustrates Remnant (Happ=0) magneto optical images at 20 K the sample field-cooled under 120 mT, in accordance with an embodiment of the present invention.

FIG. 4 illustrates the trapped field as a function of increasing temperature for the bulk sample stack that was field-cooled magnetized at 5 K and a simplified schematic of the sample and Hall probe arrangement.

FIG. 5 illustrates a magnetic hysteresis loop obtained at 5 K, in accordance with an embodiment of the present invention.

FIG. 6A illustrates the time dependence of a trapped magnetic field magnet creep at H2 and at 5 K, in accordance with an embodiment of the present invention.

FIG. 6B illustrates the normalized trapped magnetic field magnet creep at H2, as a function of time at 5, 10 and 20 K, in accordance with an embodiment of the present invention.

FIG. 7A illustrates the critical current density vs. applied magnetic field for Ba122, undoped MgB₂, and C-doped MgB₂ bulks, wherein the dotted lines are extrapolated data, in accordance with an embodiment of the present invention.

FIG. 7B illustrates the maximum trapped field vs. radius for K-doped Ba122 and MgB₂ polycrystalline bulks calculated from the data in FIG. 7A, for an infinite thickness cylinder, in accordance with an embodiment of the present invention.

DETAILED DESCRIPTION OF THE INVENTION

Permanent magnets are limited by their magnetization saturation, and are therefore not capable of producing fields much greater than 1 T. However, induced persistent currents can be trapped inside a superconductor to produce magnetic fields (B^(trapped)) that scale with the size of the current loops flowing in the bulk:

B ^(trapped) =Aμ ₀ J _(c) ^(bulk) r

where A is a geometrical factor, μ₀ is the permeability of vacuum, J_(c) ^(bulk) is the bulk or globally circulating critical current density, and r is the radius of the sample. High field bulk magnets require high J_(c) ^(bulk) and large r with a well-defined geometry. The field trapping ability is then limited mostly by J_(c)(H) (H_(c2)>90 T for Ba122)⁴ and mechanical strength.

Currently, mechanically reinforced REBCO materials produce record fields (>17 T) at modest temperatures (>20 K), but are limited in size (r≦50 mm) because grain boundaries (GBs) block current, forcing such samples to be grown as single crystals. In contrast, MgB₂ is not subject to intrinsic current blocking and can be manufactured as large diameter polycrystalline bulks, but currently, MgB₂ lacks high enough H_(c2) (limiting J_(c)(H)) to compete with YBCO for high field applications. Despite its lower T_(c) and J_(c) than YBCO and MgB₂, Ba122 has the geometric versatility of MgB₂ with better J_(c)(H) characteristics in high fields.

In a particular embodiment of the invention, Ba, K, Fe, and As were combined in a molar ratio of 0.6:0.42:2:2 and reacted together by a mechano-chemical reaction followed by sintering in a hot isostatic press (HIP) at 600° C. After the two HIP heat treatments and subsequent re-milling, approximately 3-5 g of Ba122 powder was pressed into 15.9 mm diameter pellets and then further densified in a cold isostatic press (CIP) at 276 MPa. These were then wrapped with Ag foil and inserted into a steel tube that was carefully machined to the diameter of the pellet+foil and both ends were plugged and welded shut under vacuum. The plugs were chamfered towards the pellet to help the steel tube compress around the pellet. The welded tubes were then swaged and CIPped as above, reducing the diameter of the samples ˜10%. Finally, the samples were heat treated again for 10 hours at 600° C. in the HIP. After heat treatment, the steel tubes were sliced with a diamond saw to reveal the pellet surfaces. Several room-temperature Vickers hardness (HV) measurements were made on the surface of the pellets using loads from 25 g to 2000 g. Light and scanning electron microscopy was used to study and measure the micro-indentations.

Magneto optical (MO) imaging was used to image the local field profile produced by magnetization currents induced by field-cooling into the superconducting state in 120 mT applied perpendicular to the bulk sample's surface and then removing the magnetic field. Due to the limited size of the cryostat, MO imaging was done on a 3.7 mm thick sample. Then, disk-shaped 122 bulks with ˜10 mm in diameter and ˜18.4 mm in total thickness were vertically stacked on either side of a spacer containing a transversal cryogenic Hall sensor to measure the magnetic flux density between the pellets. Another Hall sensor was mounted to the outside end of the stack. The stack was cooled to ˜5 K by a GM cryocooler under an external field (H_(app)) of 8 T, and the external field was subsequently removed. After the field-cooling magnetization and reduction of the external field to zero, the magnetic flux density trapped in the bulk was measured at the center of the spacer as a function of increasing temperature (0.2 K/min) and separately as a function of time. For the magnetic hysteresis loop measurement, the sample was zero-field cooled to 5 K and its flux density in the sample stack was recorded as a function of increasing and decreasing external field.

In a particular embodiment, the superconductors of the present invention were manufactured by hot isostatic pressing pre-reacted powders using the scalable powder-in-tube technique. Vickers hardness indentations indicate that the bulk material has high hardness of greater than about 1 GPa and a fracture toughness of greater than about 1 MPa m^(0.5). Given that the sample diameter is relatively small with Ba_(0.6)K_(0.4)Fe₂As₂ showing large irreversibility field (>90 T) and small decay of J_(c) in high fields, larger bulks are expected to trap much higher fields in excess of 10 T.

FIG. 1A illustrates a polycrystal 100 of the Fe-based superconducting permanent superconductor, in accordance with an embodiment of the present invention. The polycrystal 100 of the permanent magnet comprises randomly ordered polycrystals 105, 110. The polycrystals may be textured or untextured. FIG. 1B illustrates the polycrystalline structure of the Fe-based superconductor (122 phase) 115. The polycrystalline structure including Fe atoms 125, alkaline earth metal atoms 130 and pnictide atoms 135.

With reference to FIG. 2, the Fe-based polycrystalline superconducting permanent magnet 200 of the present invention is characterized in that in a planar surface perpendicular to magnetic field lines, the shortest distance 210 from a center of the magnetic field lines 205 to an edge of the planar surface 215 is within a range of about 1 mm to a about 10,000 mm.

To assess the mechanical properties of the Ba122 bulks, room temperature Vickers Hardness tests were performed. The average HV was 3.5 (±0.2) GPa. Cracks were observed propagating from the corners of the indentations, which is typical of brittle materials. FIG. 3A shows an optical image of one of the bulks with thickness=3.7 mm. The magnetic flux density produced by bulk current circulating over the sample is visualized in FIG. 3B and FIG. 3C by magneto optical imaging. FIG. 3B and FIG. 3C show remnant magnetic flux (H_(app)=0) from induced currents that were trapped by applying magnetic fields of 120 mT and then field-cooling the sample from above Tc to 11 K and 20 K, respectively, followed by removal of the applied magnetic field. The images show macroscopically uniform trapped field gradient at the perimeter. The light colored contrast in FIG. 3B and FIG. 3C corresponds to a high flux density perpendicular to the sample surface.

FIG. 4 shows the trapped field (at H_(app)=0) measured by Hall sensors placed on the surface (H1) and between (H2) the stack of Ba122 bulk magnets after field cooling (H_(app)=8 T) as a function of increasing temperature. It should be noted that H2 was placed 3.7 mm away from H1, which is 5.5 mm from the center of the stack where the maximum field would be expected. At 5 K, the bulk stack trapped 0.68 T on the outer surface (H1) and 1.02 T between the bulks (H2). The trapped field decreased with increasing temperature and vanished at T_(c) ˜33 K. The average macroscopic current density, which was estimated by a Biot-Savart approximation using the total thickness of the magnet stack and the experimentally obtained trapped field from H1, is ˜50 kAcm⁻². This matches J_(c) obtained by local magnetization measurements made on small bulk samples at T=4.2 K and H_(app)=0.6 T.⁹

On field cooling, no magnetic flux jumps were observed at a ramp rate of 1.8 T/h. In one instance, an unexpected quench of the magnetizing magnet resulted in a rapid (˜1 second) removal of external field from H_(app)=1.5 T to 0 T, corresponding to a ramp rate of >2 T/sec. Despite the sudden removal of flux, the trapped field value quickly shifted the expected critical state and magnet creep behavior was identical to data taken during the controlled process where H_(app) was slowly removed.

FIG. 5 shows the magnetic flux density inside the stack of the initially zero-field cooled bulk samples as a function of increasing and decreasing external field. In this embodiment, the sample was zero-field cooled to 5 K and the flux density inside the sample stack (at H2) was recorded as a function of increasing and decreasing external field. The inset shows that the hysteresis loop remains open beyond our maximum applied field of 8 T. The samples showed good shielding behavior below H_(app)=0.7 T and the hysteresis loop remained open at H_(app)>8 T (see inset), which was the maximum applied field of the magnetizing magnet.

FIG. 6A shows the time dependence of trapped field at 5 K. The trapped field decayed approximately 3% after one day at 5 K. FIG. 6B shows the normalized relaxation of trapped field as a function of time measured at 5 K, 10 K, and 20 K. The magnet creep rate increased with increased holding temperature due to thermally activated flux depinning. The trapped field decayed ˜7% after 1 day at 20 K. The flux creep state shown in FIG. 6A and FIG. 6B illustrates the weak decay of the magnetic field resulting from the intrinsic property of large K-doped Ba122. For practical use as a superconducting permanent magnet, adjustments from this critical state can be made to thermally stabilize the flux state to approximately <0.1 ppm/h, thereby providing an ultra small decay. Accordingly, after the magnetic field is trapped, either one or all of temperature, electric current, and magnet field may be controlled, to establish a more stable magnetic field than is exhibited in the critical state.

The bulk magnets were processed by a scalable and versatile low-cost technique using milling, CIPping and HIPping, which are common ceramic processing techniques used in the industry. The powder-in-tube technique and subsequent low-temperature reaction allow for several bulks to be produced in a single batch. They can then be sliced to a desired thickness, with the length and diameter of the HIP limiting the maximum bulk dimensions. In addition, the steel tubing adds a reinforcing ring that can easily be designed to further improve the mechanical strength of the bulk, as has proven invaluable for trapping high fields using REBCO bulks. High strength bulks and external reinforcement are important because the interaction between trapped field and current results in mechanical force that is proportional to J_(c)×B. Due to their brittle failure mechanics, superconductors with high fracture toughness (K_(C)) are desired for high field applications. A K_(C) of ˜2.35 (±0.14) MPa m^(0.5) was roughly calculated from the length of micro-cracks propagating from the corners of the micro-indentations according to the following formula:

$K_{C} = {0.0726\frac{P}{c^{3/2}}}$

where P is loading force in N, C is the distance between center of indention and the tip of the crack in m, and 0.0726 is a calibration constant. This fracture toughness exceeds single crystal Mn-doped Ba122, HIPped MgB₂, bulk top-seeded melt-grown YBCO, and is about equal to polycrystal Al₂O₃. Table 1 summarizes the properties of Ba122 compared to YBCO and MgB₂ bulks.

The flux distribution observed by MO imaging indicates that the current trapped in the bulks is distributed macroscopically around the entire bulk sample. No flux avalanches were observed by Hall measurements during the magnetization process, even when the magnetizing magnet quenched, as discussed above, which suggests Ba122 is less susceptible to flux jumps and avalanches than MgB₂ and YBCO bulks. This may be attributed to high thermal conductivity in the metallic Ba122 bulks or good thermal stability because of the small sample size tested here. While high H_(irr), supported by FIG. 3, suggests potential use for Ba122 bulks to trap high magnetic fields, the magnet creep rate (˜3% after a day at 5 K) is still higher than in MgB₂ (˜1.5% at 20 K)¹⁶.

FIG. 7A shows a comparison of J_(c)(H) data taken from the literature. FIG. 7B shows a calculation of maximum B^(trapped) as a function of r for K-doped Ba122 and MgB₂ using the bulk J_(c)(H) data presented in FIG. 7A. This calculation is for an infinitely long cylinder and takes the radial field dependent J_(c) into account. In the infinitely long cylinder geometry (A₀=1), local current density j(x) varies with respect to radial direction x (0<x<r) due to self-field but does not change with respect to circumferential and length directions. Thus, local flux density b(x) and j(x) can be calculated as,

b(x)=∫μ₀ j(x)dx, j(x)=J _(c)(b(x))

The maximum B^(trapped) at the center of a bulk is given as b(r). We included J_(c) data for C-doped MgB₂ bulk material, though MgB₂ bulk magnets in the literature are typically undoped and therefore have not demonstrated the ability to trap the high fields suggested by FIG. 7(b) at 4.2 K. While MgB₂ outperforms Ba122 at low fields and small r, Ba122 bulks are very competitive above the size limit of YBCO (r>50 mm) at low temperatures, and samples with r≧92 mm would be capable of trapping higher fields than MgB₂, even at 20 K. Such large bulks would be useful for magnetic levitation in energy storage applications and could provide high fields in compact magnetic resonance devices.

The trapped field at the surface of the magnetized stack of Ba122 bulks as measured by H1 was 0.68 T. The magnitude of the field at the center of the stack is expected to be approximately twice this value ˜1.36 T. H2, which measured 1.02 T, was located between H1 and the center of the stack, and is in-between 0.68 and 1.36 T. The expected central trapped field ˜1.36 T, given the radius ˜5 mm, is about 65% of the ideal maximum trapped field presented in FIG. 7B, likely due to the finite thickness of the sample and slightly lower J_(c)(H) behavior than presented in FIG. 7A.

TABLE 1 Comparison of superconducting and mechanical properties for YBCO, MgB₂ and K-doped Ba122 Fracture H_(c2) toughness Limiting T_(c) (0 K) Hardness (MPa size Material Form (K) (T) (GPa) m^(0.5)) (mm) YBCO Single 92 >100 7-8 1.4-1.6 r ~50 crystal MgB₂ Polycrystal 39 ~30 10-12 1.3-1.4 no limit Ba122 Polycrystal 38 ~90 3.5 (±0.2) 2.35 (±0.14) no limit

While high-field applications for Ba122 using much larger bulk samples look very promising, the current Ba122 bulks may not be very competitive against MgB₂ at low-fields due to their higher magnetic creep rate and lower J_(c) at low-fields. However, given improved J_(c) properties of Ba122 and Sr122 material reported in the literature, there is still a lot of room to improve J_(c) by better processing and partial alignment of grains. It is important to note that the values in FIG. 7B are proportional to J_(c)(H), so modest improvements in J_(c)(H) are all that is needed for Ba122 to be very competitive with MgB₂ even at low fields.

The methods of the present invention have been successful in synthesizing the first bulk iron-pnictide demonstration magnet capable of trapping over 1 T (5 K) and 0.5 T (20 K) by using fine-grain polycrystalline material and a scalable technique that is capable of generating much larger samples. Magneto optical imaging suggests that the novel material has macroscopic currents circulating throughout the entire sample. The time dependence of the trapped field illustrates a low magnetic creep rate (˜3% after 24 hours at 5 K). Vickers hardness indentations indicate that the bulk material has a hardness ˜3.5 GPa and a fracture toughness ˜2.35 MPa m^(0.5). Larger bulks are expected to trap even higher fields, given the high H_(c2) of K-doped BaFe₂As₂. Modest improvements to J_(c)(H) will make Ba122 bulks very competitive against REBCO and MgB₂ for permanent magnet applications.

It will be seen that the advantages set forth above, and those made apparent from the foregoing description, are efficiently attained and since certain changes may be made in the above construction without departing from the scope of the invention, it is intended that all matters contained in the foregoing description or shown in the accompanying drawings shall be interpreted as illustrative and not in a limiting sense.

It is also to be understood that the following claims are intended to cover all of the generic and specific features of the invention herein described, and all statements of the scope of the invention which, as a matter of language, might be said to fall therebetween. 

What is claimed is:
 1. A superconducting permanent magnet comprising an Fe-based polycrystal.
 2. The superconducting permanent magnet of claim 1, wherein the magnet exhibits a magnetic field greater than about 1 T at a temperature of less than about 40 K.
 3. The superconducting permanent magnet of claim 1, wherein the polycrystal comprises a square lattice of Fe forming a layered structure.
 4. The superconducting permanent magnet of claim 1, wherein the polycrystal may further comprise one or more of anion elements, including As, P, S, Se, Te, F or O.
 5. The superconducting permanent magnet of claim 1, wherein a crystalline grain of the polycrystal is smaller than about 10 μm.
 6. The superconducting permanent magnet of claim 1, wherein the polycrystal may include an untextured polycrystalline compound.
 7. The superconducting permanent magnet of claim 1, wherein the polycrystal may include a textured polycrystalline compound.
 8. The superconducting permanent magnet of claim 1, wherein a magnetic field is distributed spatially and temporally substantially homogeneously within a defined area of the permanent magnet.
 9. The superconducting permanent magnet of claim 1, wherein the polycrystal comprises a polycrystalline compound exhibiting a Vickers hardness of greater than about 1 GPa.
 10. The superconducting permanent magnet of claim 1, wherein the polycrystal comprises a polycrystalline compound exhibiting a fracture toughness of greater than about 1 MPa m^(0.5).
 11. The superconducting permanent magnet of claim 1, wherein the magnet is characterized in that in a planar surface perpendicular to magnetic field lines, the shortest distance from a center of the magnetic field lines to an edge of the planar surface is within a range of about 1 mm to a about 10,000 mm.
 12. The superconducting permanent magnet of claim 1, wherein the permanent magnet forms a composite with a conducting material or an insulating material.
 13. A superconducting permanent magnet comprising an Fe-based polycrystal, the magnet exhibiting a magnetic field greater than about 1 T at a temperature of less than about 40 K, the polycrystal of the magnet further comprising: a square lattice of Fe forming a layered structure; one or more of anion elements, including As, P, S, Se, Te, F or O; and wherein a crystalline grain of the polycrystal is smaller than about 10 μm.
 14. A method of manufacturing a superconducting permanent magnet comprising an Fe-based polycrystal, the method comprising: preparing an Fe-based powder; pressing the Fe-based powder into a first container; heat-treating the Fe-based powder in a second container to provide an Fe-based polycrystal; and magnetizing the Fe-based polycrystal to provide a superconducting permanent magnet comprising an Fe-based polycrystal at a temperature of less than about 40 K.
 15. The method of claim 14, wherein the first container and the second container are the same containers.
 16. The method of claim 14, wherein the first container and the second container are different containers.
 17. The method of claim 14, wherein magnetizing the Fe-based polycrystalline to provide an a superconducting permanent magnet comprising an Fe-based polycrystal further comprises, magnetizing the Fe-based polycrystal using a magnetic field, a pulsed magnetic field, an electric field or an electromagnetic field.
 18. The method of claim 14, wherein the Fe-based polycrystal comprises a square lattice of Fe forming a layered structure.
 19. The method of claim 14, wherein the Fe-based polycrystal may further comprise one or more of anion elements, including As, P, S, Se, Te, F or O.
 20. The method of claim 14, wherein the Fe-based polycrystal may further comprise a crystalline grain smaller than about 10 μm. 